High-strength steel sheet and method of manufacturing the same

ABSTRACT

A high-strength steel sheet has excellent workability, excellent phosphatability, and excellent corrosion resistance after electrodeposition coating has been performed, even when the contents of Si and Mn are high. Condition 1 through Condition 3 below are used when continuous annealing is performed on a steel sheet. Condition 1: In a heating process of continuous annealing, a steel sheet is heated at a heating rate of 7° C./s or more in a temperature range in an annealing furnace of 450° C. or higher and A° C. or lower (A: 500≦A). Condition 2: The maximum end-point temperature of a steel sheet is 600° C. or higher and 750° C. or lower in continuous annealing. Condition 3: In a steel sheet temperature range of 600° C. or higher and 750° C. or lower in continuous annealing, the traveling time of the steel sheet through the temperature range is 30 seconds or more and 10 minutes or less, and the dew point of the atmosphere is −10° C. or higher in the temperature range.

TECHNICAL FIELD

This disclosure relates to a high-strength steel sheet having excellent phosphatability and excellent corrosion resistance after electrodeposition coating has been performed, even when the contents of Si and Mn are high and to a method of manufacturing the steel sheet.

BACKGROUND

Nowadays, from the viewpoint of an increase in the fuel efficiency of automobiles and the collision safety of automobiles, there is a growing demand for weight reduction and strengthening of automobile bodies by increasing the strength of a material for automobile bodies to decrease the thickness of the material for automobile bodies. Therefore, the use of a high-strength steel sheet for automobiles is accelerated.

Generally, an automotive steel sheet is used in a painted state. A chemical conversion treatment called phosphating is performed on an automotive steel sheet as a pretreatment for such painting. The chemical conversion treatment of an automotive steel sheet is one of the important treatments to achieve corrosion resistance of the steel sheet after painting has been performed.

It is effective to add Si and Mn to a steel sheet to increase the strength and ductility of the steel sheet. However, when continuous annealing is performed, Si and Mn are oxidized even if annealing is performed in a reducing atmosphere of N₂+H₂ gas in which oxidation of Fe does not occur (that is, oxidized Fe is reduced). As a result of such oxidation of Si and Mn, oxides selectively containing Si and Mn (such as SiO₂ and MnO, referred to as “selective surface oxides” hereinafter) are formed in the surface of the steel sheet. Since such selective surface oxides inhibit the generation reaction of a chemical conversion film when a chemical conversion treatment is performed, a micro-region in which a chemical conversion film is not formed (also referred to as a “lack of hiding” hereinafter) is formed on the surface of the steel sheet, which results in a decrease in phosphatability.

Japanese Unexamined Patent Application Publication No. 5-320952 discloses an example of conventional techniques to increase the phosphatability of a steel sheet containing Si and Mn in which an iron coating layer having a coating weight of 20 to 1500 mg/m² is formed on the steel sheet by using an electroplating method. However, in that method, since additional electroplating equipment is needed, there is a problem of an increase in cost due to an increase in the number of processes.

In addition, phosphatability is increased by specifying a ratio Mn/Si in Japanese Patent No. 4319559, or by adding Ni in Japanese Patent No. 2951480. However, since such effects depend on the contents of Si and Mn in a steel sheet, further improvement is necessary in the case of a steel sheet having high Si and Mn contents.

Moreover, Japanese Patent No. 3840392 discloses a method in which, by controlling the dew point to be −25° C. to 0° C. when annealing is performed, an internal oxide layer consisting of oxides containing Si is formed within 1 μm from the surface of a steel sheet in the depth direction so that Si-containing oxides constitute 80% or less of a length of 10 μm on the surface of a steel sheet. However, since the method according to Japanese Patent No. 3840392 is based on the assumption that the zone in which the dew point is controlled is the whole furnace interior, it is difficult to control the dew point and, as a result, it is difficult to realize a stable operation. In addition, when annealing is performed while the dew point is unstably controlled, since there is a variation in the distribution of internal oxides formed in the steel sheet, there is concern that an irregularity in the result of a chemical conversion treatment or a lack of hiding may occur in whole or in part in the longitudinal direction or width direction of the steel sheet. Moreover, even when there is an increase in phosphatability, since Si-containing oxides exist immediately under a chemical conversion film, there is a problem of poor corrosion resistance after an electrodeposition coating has been performed in the technique according to Japanese Patent No. 3840392.

In addition, Japanese Unexamined Patent Application Publication No. 55-145122 discloses a method in which a steel sheet is heated to a temperature of 350° C. to 650° C. in an oxidizing atmosphere to form an oxide film on the surface of the steel sheet, then heated to the recrystallization temperature in a reducing atmosphere, and then cooled. However, in that method, since the thickness of the oxide film formed on the surface of the steel sheet varies depending on an oxidizing method, oxidizing may not sufficiently progress. In addition, in the method according to Japanese Unexamined Patent Application Publication No. 55-145122, when the thickness of oxide film formed is so large that the oxide film is retained or flaking of the oxide film occurs when annealing is subsequently performed in a reducing atmosphere, this may result in a decrease in surface quality. In addition, in the EXAMPLES of Japanese Unexamined Patent Application Publication No. 55-145122, a technique in which oxidation is performed in atmospheric air is described. However, in oxidation in atmospheric air, since a thick oxide is formed, there is a problem in that it is difficult to subsequently perform reduction or in that a reducing atmosphere having a high hydrogen concentration is needed.

Moreover, Japanese Unexamined Patent Application Publication No. 2006-45615 discloses a method in which a cold-rolled steel sheet containing, by mass %, 0.1% or more of Si and/or 1.0% or more of Mn is heated to a temperature of 400° C. or higher in an iron-oxidizing atmosphere to form an oxide film on the surface of the steel sheet, and the oxide film on the surface of the steel sheet described above is subsequently reduced in an iron-reducing atmosphere. Specifically, Fe on the surface of a steel sheet is oxidized at a temperature of 400° C. or higher by using direct fire burners in an atmosphere having an air ratio of 0.93 or more and 1.10 or less, and then the steel sheet is annealed in an iron-reducing atmosphere of N₂+H₂ gas, which reduces oxidized Fe. With that method, formation of selective surface oxides, which decrease phosphatability, on the surface of the steel sheet is inhibited so that an Fe oxide layer is formed on the surface of the steel sheet. The heating temperature of the direct fire burners is not specifically described in Japanese Unexamined Patent Application Publication No. 2006-45615. However, when the Si content is high (about 0.6% or more) in Japanese Unexamined Patent Application Publication No. 2006-45615, since Si is more likely to be oxidized than Fe, there is an increase in the amount of Si oxidized, which results in the oxidation of Fe being inhibited or results in an excessive decrease in the amount of Fe oxidized. As a result, in the technique according to Japanese Unexamined Patent Application Publication No. 2006-45615, the layer of reduced Fe is insufficiently formed on the surface after reduction has been performed, or SiO₂ exists on the surface of the steel sheet after reduction has been performed, which may result in a lack of hiding occurring in a chemical conversion film.

It could therefore be helpful to provide a high-strength steel sheet having excellent workability, excellent phosphatability, and excellent corrosion resistance after electrodeposition coating has been performed, even when the contents of Si and Mn are high, and to provide a method of manufacturing the steel sheet.

SUMMARY

In conventional techniques, by simply increasing water vapor partial pressure or oxygen partial pressure of the whole annealing furnace interior to increase the dew point or oxygen concentration, the inside of a steel sheet is excessively oxidized. Therefore, as described above, in conventional techniques, there is a problem of a decrease in controllability of dew point or oxidation in a whole furnace interior, an irregularity in the result of a chemical conversion treatment, or a decrease in corrosion resistance after electrodeposition coating has been performed.

We found that, by performing higher-level control on the microstructure or structure of a steel sheet surface layer, which may become the starting point at which a decrease in corrosion resistance after electrodeposition coating has been performed occurs, there is an increase in the phosphatability and corrosion resistance after electrodeposition coating has been performed of a high-strength steel sheet. Specifically, Condition 1 through Condition 3 below are used when continuous annealing is performed on a steel sheet.

Condition 1 In a heating process of continuous annealing, a steel sheet is heated at a heating rate of 7° C./sec. or more in a temperature range in an annealing furnace of 450° C. or higher and A° C. or lower (A: 500≦A).

Condition 2 The maximum end-point temperature of a steel sheet is 600° C. or higher and 750° C. or lower in continuous annealing.

Condition 3 In a steel sheet temperature range of 600° C. or higher and 750° C. or lower in continuous annealing, the traveling time of the steel sheet through the temperature range is 30 seconds or more and 10 minutes or less, and the dew point of the atmosphere is −10° C. or higher in the temperature range.

By performing such treatments, it is possible to inhibit the selective surface diffusion and oxidation (hereinafter, referred to as “surface concentration”) of, for example, Si and Mn. As a result, it is possible to obtain a high-strength steel sheet excellent in terms of phosphatability, workability, and corrosion resistance after electrodeposition coating has been performed.

The microstructure or structure of the steel sheet surface layer of a high-strength steel sheet obtained by using the method described above has Characteristic 1 and Characteristic 2 below.

Characteristic 1 In a region within 100 μm from the surface of the high-strength steel sheet, the oxides of at least one selected from among Fe, Si, Mn, Al, P, B, Nb, Ti, Cr, Mo, Cu, Ni, Sn, Sb, Ta, W, and V is contained in an amount of 0.010 g/m² or more and 0.050 g/m² or less per side in total.

Characteristic 2 In an intra-grain region within 1 μm from the grain boundary of a steel sheet crystal grain existing in a region within 10 μm from the surface of the steel sheet, oxides containing crystalline Mn-based oxides are contained.

By forming a steel sheet surface layer having such characteristics, it is possible to achieve excellent phosphatability to inhibit a decrease in corrosion resistance after electrodeposition coating has been performed.

We thus provide:

(1) A method of manufacturing a high-strength steel sheet, the method including, when a steel sheet having a chemical composition containing, by mass %, C: 0.03% or more and 0.35% or less, Si: 0.01% or more and 0.50% or less, Mn: 3.6% or more and 8.0% or less, Al: 0.01% or more and 1.0% or less, P: 0.10% or less, S: 0.010% or less, and the balance being Fe and inevitable impurities is annealed in a continuous annealing process, performing heating the steel sheet in a heating process of the continuous annealing process at a heating rate of 7° C./sec. or more in a temperature range in an annealing furnace of 450° C. or higher and A° C. or lower (A: 500≦A), controlling the maximum end-point temperature of a steel sheet in the continuous annealing process to be 600° C. or higher and 750° C. or lower, and controlling, in a steel sheet temperature range of 600° C. or higher and 750° C. or lower in the continuous annealing process, a traveling time of the steel sheet through the temperature range to be 30 seconds or more and 10 minutes or less and a dew point of an atmosphere to be −10° C. or higher in the temperature range.

(2) The method of manufacturing a high-strength steel sheet according to item (1), the steel sheet having the chemical composition further containing, by mass %, one or more chemical elements selected from among B: 0.001% or more and 0.005% or less, Nb: 0.005% or more and 0.05% or less, Ti: 0.005% or more and 0.05% or less, Cr: 0.001% or more and 1.0% or less, Mo: 0.05% or more and 1.0% or less, Cu: 0.05% or more and 1.0% or less, Ni: 0.05% or more and 1.0% or less, Sn: 0.001% or more and 0.20% or less, Sb: 0.001% or more and 0.20% or less, Ta: 0.001% or more and 0.10% or less, W: 0.001% or more and 0.10% or less, and V: 0.001% or more and 0.10% or less.

(3) The method of manufacturing a high-strength steel sheet according to item (1) or (2), the method further including performing electrolytic pickling in an aqueous solution containing sulfuric acid after the continuous annealing process has been performed.

(4) A high-strength steel sheet having the chemical composition according to item (1) or (2), the oxides of at least one or more selected from among Fe, Si, Mn, Al, P, B, Nb, Ti, Cr, Mo, Cu, Ni, Sn, Sb, Ta, W, and V in an amount of 0.010 g/m² or more and 0.050 g/m² or less per side in total in a region within 100 μm from the surface of the steel sheet, and oxides containing Mn in an intra-grain region within 1 μm from a grain boundary of a steel sheet crystal grain existing in a region within 10 μm from the surface of the steel sheet.

It is possible to obtain a high-strength steel sheet having excellent workability, excellent phosphatability, and excellent corrosion resistance after electrodeposition coating has been performed, even when the contents of Si and Mn are high.

In addition, it is also possible to obtain a high-strength steel sheet having not only an excellent appearance quality but also excellent workability, excellent phosphatability, and excellent corrosion resistance after electrodeposition coating has been performed.

“Excellent phosphatability” refers to when a steel sheet has an appearance quality without a lack of hiding or a surface irregularity as a result of a chemical conversion treatment. By inhibiting the lack of hiding and the surface irregularity from occurring, it is possible to achieve an excellent appearance quality.

DETAILED DESCRIPTION

Hereafter, our steel sheets and methods will be described. This disclosure is not, however, limited to the examples described below.

The method of manufacturing the high-strength steel sheet uses Condition 1 through Condition 3 below when continuous annealing is performed on a steel sheet.

Condition 1 In a heating process of continuous annealing, a steel sheet is heated at a heating rate of 7° C./sec. or more in a temperature range in an annealing furnace of 450° C. or higher and A° C. or lower (500≦A).

Condition 2 The maximum end-point temperature of a steel sheet is 600° C. or higher and 750° C. or lower in continuous annealing.

Condition 3 In a temperature range of 600° C. or higher and 750° C. or lower in terms of the temperature of a steel sheet in continuous annealing, the traveling time of the steel sheet through the temperature range is 30 seconds or more and 10 minutes or less, and the dew point of the atmosphere is −10° C. or higher in the temperature range.

First, a method of manufacturing a steel sheet to be subjected to continuous annealing will be described. There is no particular limitation on what method is used to manufacture the steel sheet. For example, a method in which a hot-rolled steel sheet is manufactured by performing hot rolling on steel, a method in which a cold-rolled steel sheet is manufactured by performing hot rolling followed by cold rolling on steel, or a method in which a cold-rolled steel sheet is manufactured by performing hot rolling followed by pickling and subsequent cold rolling on steel may be used. A hot-rolled steel sheet or a cold-rolled steel sheet having been manufactured as described above may be used as a steel sheet to be subjected to continuous annealing.

There is no particular limitation on what conditions are used for hot rolling and pickling when the steel sheet described above is manufactured, and these conditions may be appropriately set. In addition, it is preferable that cold rolling be performed with a rolling reduction of 40% or more and 80% or less. When the rolling reduction is less than 40%, since the recrystallization temperature is lowered, there is a tendency for mechanical properties to deteriorate. On the other hand, when the rolling reduction is more than 80%, there is an increase in rolling costs because high-strength steel sheet is rolled, and there may be a decrease in phosphatability due to an increase in the degree of surface concentration when annealing is performed.

Subsequently, a process in which a steel sheet is subjected to continuous annealing will be described. Continuous annealing may be performed by using general continuous annealing equipment. An annealing furnace installed in general continuous annealing equipment has a heating zone in the front part of the furnace and a soaking zone in the rear part of the furnace. Usually, a steel sheet is heated to a specified temperature in a heating zone in the front part of the furnace and held at a specified temperature for a specified time in a soaking zone in the rear part of the furnace.

We use Condition 1 through Condition 3 described above when continuous annealing is performed.

As described in Condition 1 above, in a heating process of continuous annealing, heating is performed while a heating rate is controlled to be 7° C./sec. or more in a temperature range in an annealing furnace of 450° C. or higher and A° C. or lower (A: 500≦A). By performing heating in such a manner, since it is possible to pass a steel sheet as fast as possible through a temperature range of 450° C. or higher and A° C. or lower (A: 500≦A), in which surface concentration of easily oxidizable chemical elements occurs (such as Si and Mn) while oxidation thereof inside a steel sheet (hereinafter, referred to as “internal oxidation”) does not occur, it is possible to inhibit surface concentration. That is, it is possible to inhibit, for example, a lack of hiding and surface irregularity as a result of a chemical conversion treatment.

The effect of increasing phosphatability described above is realized by using all of Condition 1 through Condition 3. In particular, it is considered that Condition 1 and Condition 3 are important. As described above, by using Condition 1, formation of surface-concentration matter is inhibited as much as possible. Moreover, by using Condition 3, it is possible to inhibit the surface concentration of, for example, Si and Mn in steel, which decrease phosphatability after annealing has been performed, in a steel sheet surface by forming an appropriate amount of internal oxides in a region inside a steel sheet within 10 μm from the surface of the steel sheet. By using these conditions, it is possible to achieve excellent phosphatability without a lack of hiding or surface irregularity and higher corrosion resistance after electrodeposition coating has been performed.

The reasons for using Condition 1 through Condition 3 will be specifically described hereafter.

As described in Condition 1 above, in a heating process of continuous annealing, a heating rate is controlled to be 7° C./sec. or more in a temperature range in an annealing furnace of 450° C. or higher and A° C. or lower (where A: a value satisfying the relationship 500≦A). Usually, this heating is performed in a heating zone. The temperature in this temperature range refers to the temperature of a steel sheet (steel sheet temperature) being annealed. A steel sheet temperature may be defined as a temperature determined by using a thermometer placed at a position of a roll of each pass in an annealing furnace. Examples of such a thermometer include a multiple reflection-type thermometer and a radiation thermometer, and there is no particular limitation on the type of a thermometer.

The reason why the temperature range in which the heating rate is controlled is a temperature range of 450° C. or higher is as follows. The level of surface concentration or internal oxidation occurring in a temperature range lower than 450° C. is not high enough to cause, for example, a lack of hiding, surface irregularity, or a decrease in corrosion resistance having a negative effect. Therefore, the temperature range in which the heating rate is controlled is a temperature range of 450° C. or higher in which the desired effect is realized.

In addition, the reason why the temperature range in which the heating rate is controlled is a temperature range of A° C. or lower (where A: a value satisfying the relationship 500≦A) is as follows. First, when the upper limit of the temperature range in which the heating rate is controlled is lower than 500° C., since the time for which the heating rate is controlled to be 7° C./sec. or more is short, the desired effect is insufficiently realized. Therefore, A is 500° C. or higher. In addition, when the upper limit of the temperature range in which the heating rate is controlled is higher than 600° C., there is no problem with the desired effect. However, when the upper limit is higher than 600° C., there is a disadvantage from the viewpoint of an increase in the cost for devices in an annealing furnace (such as an additional induction heater). Therefore, it is preferable that the upper limit be 600° C. or lower.

The reason why the heating rate is controlled to be 7° C./sec. or more in the temperature range described above is as follows. The effect of inhibiting surface concentration is realized when the heating rate is 7° C./sec. or more. Although there is no particular limitation on the upper limit of the heating rate, when the heating rate is 500° C./sec. or more, since the effect becomes saturated, there is an economic disadvantage. Therefore, it is preferable that the heating rate be 500° C./sec. or less. It is possible to control the heating rate to be 7° C./sec. or more by placing, for example, an induction heater in the region of the annealing furnace where the steel sheet temperature is 450° C. or higher and A° C. or lower.

As described in Condition 2 above, the maximum end-point temperature of a steel sheet is controlled to be 600° C. or higher and 750° C. or lower in annealing. The maximum end-point temperature of a steel sheet described above is, unless A° C. is equal to the maximum end-point temperature of a steel sheet, a temperature reached by further performing heating from A° C. which is the maximum end-point temperature reached by heating in the heating process described above. “Maximum end-point temperature of steel sheet” refers to the maximum temperature in annealing when a temperature is determined by using a method similar to that used to determine the steel sheet temperature described above.

The reason why the maximum end-point temperature of the steel sheet in the annealing furnace is controlled to be 600° C. or higher and 750° C. or lower is as follows. When the maximum end-point temperature of a steel sheet is lower than 600° C., it is not possible to achieve good material properties. Therefore, the maximum end-point temperature of a steel sheet is 600° C. or higher. On the other hand, when the maximum end-point temperature of a steel sheet is higher than 750° C., since surface concentration becomes marked, for example, a decrease in phosphatability begins to be recognizable. Moreover, from the viewpoint of material properties, when the maximum end-point temperature of a steel sheet is higher than 750° C., the effect of a strength-ductility balance becomes saturated. Therefore, the maximum end-point temperature of the steel sheet is 600° C. or higher and 750° C. or lower.

As described in Condition 3 above, in a steel sheet temperature range of 600° C. or higher and 750° C. or lower in continuous annealing, the traveling time of the steel sheet through the temperature range is controlled to be 30 seconds or more and 10 minutes or less, and the dew point of the atmosphere is controlled to be −10° C. or higher in the temperature range.

When the above-described traveling time of the steel sheet is less than 30 seconds, it is not possible to achieve the target material properties (TS and El). On the other hand, when the above-described traveling time of the steel sheet is more than 10 minutes, the effect of a strength-ductility balance becomes saturated.

When the dew point of the atmosphere in a steel sheet temperature range of 600° C. or higher and 750° C. or lower in annealing is −10° C. or higher, since there is an increase in the potential of O₂, which is generated by the decomposition of H₂O, due to a rise in the dew point, it is possible to promote internal oxidation. In a temperature range lower than −10° C., there is a decrease in the amount of internal oxidation. In addition, there is no particular limitation on the upper limit of the dew point. However, when the dew point is higher than 90° C., since there is an increase in the amount of Fe oxidized, there is a risk of the deterioration of the surface walls of an annealing furnace or rolls. Therefore, it is preferable that the dew point be 90° C. or lower.

There is no particular limitation on the dew point in other temperature ranges, and the dew point may be, for example, −10° C. to −40° C.

In an annealing process, using Condition 1 through Condition 3 described above is important to obtain a high-strength steel sheet having excellent phosphatability and excellent corrosion resistance after electrodeposition coating has been performed. Annealing conditions other than the essential conditions described above are as follows.

There is no particular limitation on a soaking temperature or a soaking time in the soaking zone, and these conditions may be appropriately set.

In the continuous annealing process described above, there is no particular limitation on an atmospheric gas as long as the desired effect is not decreased. Usually, the atmospheric gas contains hydrogen gas, nitrogen gas, and inevitable impurity gases. In addition, gases other than the above-mentioned gases (for example, H₂O, CO₂, and CO) may be contained as long as the desired effect is not decreased.

It is preferable that the hydrogen concentration in the atmosphere for continuous annealing be 1 vol % or more and 50 vol % or less. When the hydrogen concentration is less than 1 vol %, since it is not possible to realize an activation effect due to reduction, there may be a decrease in phosphatability. Although there is no particular limitation on the upper limit of the hydrogen concentration, when the hydrogen concentration is more than 50 vol %, there is an increase in manufacturing costs to increase the hydrogen concentration, and the effect due to the control of hydrogen concentration becomes saturated. Therefore, it is preferable that the hydrogen concentration be 1 vol % or more and 50 vol % or less, or more preferably 5 vol % or more and 30 vol % or less.

In the manufacturing method, the following treatments may be performed after continuous annealing has been performed.

After cooling the high-strength steel sheet from the temperature range of 600° C. or higher and 750° C. or lower, quenching and tempering may be performed as needed. There is no particular limitation on what conditions are used for quenching and tempering. It is preferable that tempering be performed at a temperature of 150° C. or higher and 400° C. or lower. There is a tendency for elongation of the steel sheet to decrease when tempering temperature is lower than 150° C., and there is a tendency for hardness of the steel sheet to decrease when the tempering temperature is higher than 400° C.

In addition, it is possible to achieve good phosphatability, even when electrolytic pickling is not performed. However, to achieve better phosphatability by removing a small amount of surface-concentration matter inevitably formed when annealing is performed, it is preferable that electrolytic pickling be performed in an aqueous solution containing sulfuric acid on the high-strength steel sheet after continuous annealing has been performed.

There is no particular limitation on what kind of pickling solution is used for electrolytic pickling. However, nitric acid or hydrofluoric acid is not preferable, because it is necessary to carefully handle such kinds of acids because such kinds of acids have a strong corrosive effect on equipment. In addition, hydrochloric acid is not preferable, because chlorine gas may be generated from a cathode. Therefore, it is preferable to use sulfuric acid in consideration of corrosiveness and the environment. It is preferable that the sulfuric acid concentration be 5 mass % or more and 20 mass % or less. When the sulfuric acid concentration is less than 5 mass %, since there is a decrease in electrical conductivity, there may be an increase in power load due to an increase in bath voltage when an electrolytic reaction occurs. On the other hand, when the sulfuric acid concentration is more than 20 mass %, since there is an increase in loss due to drag-out, there is a cost problem.

There is no particular limitation on what condition is used for electrolytic pickling. To efficiently remove oxides of Si and Mn inevitably formed and concentrated on the surface after annealing has been performed, it is preferable that alternate current electrolysis be performed with a current density of 1 A/dm² or more. The reason why alternate current electrolysis is performed is as follows. When the steel sheet is held at the cathode, there is an insufficient effect of pickling. In addition, when the steel sheet is held at the anode, since Fe which is eluted when electrolysis is performed is accumulated in the pickling solution, there is an increase in Fe concentration in the pickling solution, which results in problems such as dry staining due to the adhesion of Fe to the surface of the steel sheet.

It is preferable that the temperature of the electrolyte solution be 40° C. or higher and 70° C. or lower. Since there is an increase in bath temperature due to the heat generation caused by continuous electrolysis, it may be difficult to keep the temperature lower than 40° C. In addition, from the viewpoint of the durability of the lining of the electrolysis bath, it is not preferable that the temperature be higher than 70° C. Since there is an insufficient pickling effect when the temperature is lower than 40° C., it is preferable that the temperature be 40° C. or higher.

As described above, we provide a manufacturing method characterized by the continuous annealing conditions of a steel sheet. The steel sheet to be subjected to such continuous annealing will be described. Hereinafter, “%” used when describing a chemical composition refers to “mass %”.

C: 0.03% or More and 0.35% or Less

C increases workability by forming, for example, martensite in a steel microstructure. It is necessary that the C content be 0.03% or more to realize such an effect. On the other hand, when the C content is more than 0.35%, there is a decrease in elongation due to an increase in strength, which results in a decrease in workability. Therefore, the C content is 0.03% or more and 0.35% or less.

Si: 0.01% or More and 0.50% or Less

Si is a chemical element effective in achieving good material properties by increasing the strength of steel. However, since Si is an easily oxidizable chemical element, Si is disadvantageous for a chemical conversion treatment. From this point of view, the addition of Si should be avoided as much as possible. In addition, since Si is inevitably contained in steel in an amount of about 0.01%, there is an increase in cost to control the Si content to be less than 0.01%. Therefore, the lower limit of the Si content is 0.01%. On the other hand, when the Si content is more than 0.50%, the effect of increasing the strength and elongation of steel becomes saturated, and there is a decrease in the phosphatability of a high-strength steel sheet. Therefore, the Si content is 0.01% or more and 0.50% or less. The fact that it is possible to increase phosphatability even when the Si content is large is one of the characteristics of our method.

Mn: 3.6% or More and 8.0% or Less

Mn is a chemical element effective to increase the strength of steel. It is necessary that the Mn content be 3.6% or more to achieve satisfactory mechanical properties and strength. On the other hand, when the Mn content is more than 8.0%, it is difficult to achieve satisfactory phosphatability and a satisfactory strength-ductility balance, and there is an economic disadvantage. Therefore, the Mn content is 3.6% or more and 8.0% or less.

Al: 0.01% or More and 1.0% or Less

Al is added to deoxidize molten steel. However, when the Al content is less than 0.01%, such an object is not realized. The effect of deoxidizing molten steel is realized when the Al content is 0.01% or more. On the other hand, when the Al content is more than 1.0%, there is an increase in cost. Moreover, when the Al content is more than 1.0%, it is difficult to increase phosphatability due to an increase in the amount of the surface concentration of Al. Therefore, the Al content is 0.01% or more and 1.0% or less.

P: 0.10% or Less

Since P is one of the chemical elements inevitably contained, it is not necessary that P be contained. Since there may be an increase in cost to control the P content to be less than 0.005%, it is preferable that the P content be 0.005% or more. On the other hand, when the P content is more than 0.10%, there is a decrease in weldability. In addition, when the P content is more than 0.10%, it is difficult to increase phosphatability even by using our method due to a significant decrease in phosphatability. Therefore, the P content is 0.10% or less, and it is preferable that the lower limit of the P content is 0.005%.

S: 0.010% or Less

Since S is one of the chemical elements which are inevitably contained, it is not necessary that S be contained. Therefore, there is no particular limitation on the lower limit of the S content. When the S content is large, there is a decrease in weldability and corrosion resistance. Therefore, the S content is 0.010% or less.

In addition, one or more chemical elements selected from among B: 0.001% or more and 0.005% or less, Nb: 0.005% or more and 0.05% or less, Ti: 0.005% or more and 0.05% or less, Cr: 0.001% or more and 1.0% or less, Mo: 0.05% or more and 1.0% or less, Cu: 0.05% or more and 1.0% or less, Ni: 0.05% or more and 1.0% or less, Sn: 0.001% or more and 0.20% or less, Sb: 0.001% or more and 0.20% or less, Ta: 0.001% or more and 0.10% or less, W: 0.001% or more and 0.10% or less, and V: 0.001% or more and 0.10% or less may be added in a steel sheet to be subjected to continuous annealing as needed to improve the surface quality and strength-ductility balance of a high-strength steel sheet manufactured by using the manufacturing method. When these chemical elements are added, the reasons of the limitation on the appropriate amounts of these chemical elements added are as follows.

B: 0.001% or More and 0.005% or Less

When the B content is less than 0.001%, it is difficult to realize the effect of promoting hardenability. On the other hand, when the B content is more than 0.005%, there may be a decrease in phosphatability. Therefore, when B is added, it is preferable that the B content be 0.001% or more and 0.005% or less. However, when it is considered that it is not necessary to add B to improve mechanical properties, a steel sheet does not have to contain B. Also, the other optional constituent chemical elements are added as needed.

Nb: 0.005% or More and 0.05% or Less

When the Nb content is less than 0.005%, it is difficult to realize the effect of controlling strength. On the other hand, when the Nb content is more than 0.05%, there is an increase in cost. Therefore, when Nb is added, the Nb content is 0.005% or more and 0.05% or less.

Ti: 0.005% or More and 0.05% or Less

When the Ti content is less than 0.005%, it is difficult to realize the effect of controlling strength. On the other hand, when the Ti content is more than 0.05%, there may be a decrease in phosphatability. Therefore, when Ti is added, it is preferable that the Ti content be 0.005% or more and 0.05% or less.

Cr: 0.001% or More and 1.0% or Less

It is difficult to realize the effect of hardenability when the Cr content is less than 0.001%. On the other hand, when the Cr content is more than 1.0%, since Cr is concentrated on the surface, there is a decrease in weldability. Therefore, when Cr is added, it is preferable that the Cr content be 0.001% or more and 1.0% or less.

Mo: 0.05% or More and 1.0% or Less

It is difficult to realize the effect of controlling strength when the Mo content is less than 0.05%. On the other hand, when the Mo content is more than 1.0%, there is an increase in cost. Therefore, when Mo is added, it is preferable that the Mo content be 0.05% or more and 1.0% or less.

Cu: 0.05% or More and 1.0% or Less

When the Cu content is less than 0.05%, it is difficult to realize the effect of promoting the formation of a retained γ phase. On the other hand, when the Cu content is more than 1.0%, there is an increase in cost. Therefore, when Cu is added, it is preferable that the Cu content is 0.05% or more and 1.0% or less.

Ni: 0.05% or More and 1.0% or Less

It is difficult to realize the effect of promoting the formation of a retained γ phase when the Ni content is less than 0.05%. On the other hand, when the Ni content is more than 1.0%, there is an increase in cost. Therefore, when Ni is added, it is preferable that the Ni content be 0.05% or more and 1.0% or less.

Sn: 0.001% or More and 0.20% or Less and Sb: 0.001% or More and 0.20% or Less

Sn and Sb may be added to inhibit the nitration or oxidation of the surface of a steel sheet or the decarburization due to oxidation of a region within several tens of micrometers of the surface of a steel sheet. By inhibiting nitration and oxidation, a decrease in the amount of martensite formed in the surface of a steel sheet is prevented and there is an increase in the fatigue characteristic and surface quality of a high-strength steel sheet obtained. From the viewpoint described above, when Sn and/or Sb are added, it is preferable that each of the contents of these chemical elements be 0.001% or more. In addition, since there is a decrease in toughness when any one of the contents of these chemical elements is more than 0.20%, it is preferable that each of the contents of these chemical elements be 0.20% or less.

Ta: 0.001% or More and 0.10% or Less

Ta contributes to an increase in strength by combining with C and N to form carbides and carbonitrides and to an increase in yield ratio (YR). Moreover, since Ta is effective to decrease the grain diameter of the microstructure of a hot-rolled steel sheet, there is a decrease in the ferrite grain diameter of the steel sheet due to such an effect after cold rolling or annealing has been performed. In addition, since there is an increase in the amount of C segregated at the grain boundaries due to an increase in the area of the grain boundaries, it is possible to achieve a large amount of bake hardening (BH amount). From such viewpoints, Ta may be added in an amount of 0.001% or more. On the other hand, when the Ta content is more than 0.10%, there is a risk in that formation of martensite is obstructed in a cooling process following an annealing process in addition to an increase in the raw material cost. Moreover, since TaC precipitated in a hot-rolled steel sheet may increase resistance to deformation when cold rolling is performed, it may be difficult to stably manufacture steel sheets in a practical line. Therefore, when Ta is added, it is preferable that the Ta content be 0.10% or less.

W: 0.001% or More and 0.10% or Less and V: 0.001% or More and 0.10% or Less

W and V, which are chemical elements effective for increasing the strength of steel through a precipitation effect by forming carbonitrides, may be added as needed. When W and/or V are added, such an effect is observed when each of the contents of these chemical elements is 0.001% or more. On the other hand, when any one of the contents of these chemical elements is more than 0.10%, there may be a decrease in ductility due to an excessive increase in the strength of a steel sheet. Therefore, when W and/or V are added, it is preferable that each of the contents of these chemical elements be 0.001% or more and 0.10% or less.

The remaining constituent chemical elements other than those described above are Fe and inevitable impurities. There is no negative effect even when chemical elements other than those described above are added, and the upper limit of the content is 0.10%.

By controlling the conditions of continuous annealing of a steel sheet having the chemical composition described above, it is possible to obtain a high-strength steel sheet excellent in terms of workability, phosphatability, and corrosion resistance after electrodeposition coating has been performed. Hereafter, such a high-strength steel sheet will be described.

It is necessary to perform higher-level control on the microstructure or structure of a steel sheet surface layer, which may become the starting point at which, for example, corrosion cracking occurs, to achieve satisfactory corrosion resistance after electrodeposition coating has been performed in a high-strength steel sheet containing Si and large amounts of Mn. Therefore, first, to achieve satisfactory phosphatability, oxygen potential is increased by controlling the dew point in continuous annealing. By increasing oxygen potential, since easily oxidizable chemical elements such as Si and Mn undergo internal oxidation in advance immediately before a chemical conversion treatment is performed, there is a decrease in the activity of Si and Mn on the surface of a steel sheet. In addition, the external oxidation of such chemical elements is inhibited, which results in an increase in phosphatability and corrosion resistance after electrodeposition coating has been performed. Specifically, the microstructure or structure of the steel sheet surface layer of a high-strength steel sheet manufactured by using our manufacturing method has the following characteristics.

Characteristic 1 In a region within 100 μm from the surface of the high-strength steel sheet, the oxides of at least one or more selected from among Fe, Si, Mn, Al, P, B, Nb, Ti, Cr, Mo, Cu, Ni, Sn, Sb, Ta, W, and V are contained in an amount of 0.010 g/m² or more and 0.050 g/m² or less per side in total.

Characteristic 2 In an intra-grain region within 1 μm from the grain boundary of a steel sheet crystal grain existing in a region within 10 μm from the surface of the steel sheet, oxides containing Mn are contained.

As described in Characteristic 1 above, in a region within 100 μm from the surface of the high-strength steel sheet, the oxides of at least one or more selected from among Fe, Si, Mn, Al, P, B, Nb, Ti, Cr, Mo, Cu, Ni, Sn, Sb, Ta, W, and V are contained in an amount of 0.010 g/m² or more per side in total. With this characteristic, there is an increase in phosphatability and corrosion resistance after electrodeposition coating has been performed. When the amount of the formed oxides is more than 0.050 g/m², there is concern that the oxide may become the starting point at which corrosion cracking occurs. In addition, when the amount of the oxides formed is more than 0.050 g/m², since the effect of increasing phosphatability becomes saturated, it is not necessary that the amount of the oxides formed be more than 0.050 g/m².

As described in Characteristic 2 above, in an intra-grain region within 1 μm from the grain boundary of a steel sheet crystal grain existing in a region within 10 μm from the surface of the steel sheet, oxides containing Mn are contained. When internal oxides exist only at grain boundaries and where internal oxides do not exist in grains, although it is possible to inhibit the grain boundary diffusion of easily oxidizable chemical elements in steel, it may not be possible to sufficiently inhibit the intra-grain diffusion of such chemical elements. Therefore, as described above, by controlling a heating rate to be 7° C./sec. or more in a temperature range in an annealing furnace of 450° C. or higher and A° C. or lower (A: 500≦A), internal oxidation occurs not only at grain boundaries but also in grains. Specifically, in an intra-grain region within 1 μm from the grain boundary of a base steel sheet crystal grain existing in a region within 10 μm from the surface of the steel sheet, crystalline Si- and Mn-based oxides are contained. As a result of oxides existing in the grains described above, there is a decrease in the amount of a solid solution Si and a solid solution Mn in grains in the vicinity of the oxides. As a result, it is possible to inhibit the surface concentration of Si and Mn due to the intra-grain diffusion of Si and Mn.

Although the structure of the steel sheet surface of the high-strength steel sheet obtained by using our manufacturing method is as described above, there is no problem in that, for example, the oxides described above grow in a region more than 100 μm from the surface of a steel sheet. In addition, there is no problem in that, in an intra-grain region located at 1 μm or more from the grain boundary existing in a region located at more than 10 μm from the surface of a steel sheet, crystalline Si- and Mn-based oxides exist.

The high-strength steel sheet may be manufactured by performing a chemical conversion treatment on the high-strength steel sheet described above. There is no particular limitation on the kinds of a chemical conversion treatment solution, and a general solution such as a chromate treatment solution or a non-chromate treatment solution may be used. In addition, there is no particular limitation on what method is used for a chemical conversion treatment, any of various kinds of methods such as an immersing (dipping) treatment, a spraying treatment, and an electrolysis treatment may be used.

The high-strength steel sheet may be manufactured by forming a coating film on a chemical conversion film of the steel sheet subjected to a chemical conversion treatment by performing electrodeposition coating. There is no particular limitation on what condition is used for electrodeposition coating, and the condition may be appropriately specified.

EXAMPLES

Hereafter, our steel sheets and methods will be specifically described on the basis of examples.

By pickling hot-rolled steel sheets having the steel chemical composition given in Table 1 to remove black scale, by then performing cold rolling on the pickled steel sheets, cold-rolled steel sheets having a thickness of 1.0 mm were obtained. Some of the steel sheets were not subjected to cold rolling and left as hot-rolled steel sheets (having a thickness of 2.0 mm) from which black scale had been removed.

TABLE 1 (mass %) Steel Code C Si Mn Al P S Cr Mo B Nb Cu Ni Ti Sn Sb Ta W V A 0.12 0.03 4.5 0.03 0.01 0.004 — — — — — — — — — — — — B 0.03 0.03 4.6 0.03 0.01 0.004 — — — — — — — — — — — — C 0.35 0.03 4.7 0.02 0.01 0.004 — — — — — — — — — — — — D 0.12 0.10 4.5 0.03 0.01 0.004 — — — — — — — — — — — — E 0.13 0.30 4.7 0.04 0.01 0.004 — — — — — — — — — — — — F 0.12 0.50 4.6 0.03 0.01 0.004 — — — — — — — — — — — — G 0.12 0.03 3.6 0.02 0.01 0.004 — — — — — — — — — — — — H 0.13 0.03 6.3 0.03 0.01 0.004 — — — — — — — — — — — — I 0.12 0.03 8.0 0.02 0.01 0.004 — — — — — — — — — — — — J 0.13 0.03 4.5 0.30 0.01 0.004 — — — — — — — — — — — — K 0.12 0.03 4.6 1.00 0.01 0.004 — — — — — — — — — — — — L 0.12 0.03 4.7 0.03 0.05 0.004 — — — — — — — — — — — — M 0.12 0.03 4.5 0.02 0.10 0.004 — — — — — — — — — — — — N 0.13 0.02 4.7 0.03 0.01 0.009 — — — — — — — — — — — — O 0.12 0.03 4.6 0.02 0.01 0.004 0.8 — — — — — — — — — — — P 0.13 0.03 4.5 0.03 0.01 0.004 — 0.1 — — — — — — — — — — Q 0.13 0.02 4.7 0.03 0.01 0.004 — — 0.003 — — — — — — — — — R 0.12 0.03 4.5 0.05 0.01 0.004 — — 0.001 0.03 — — — — — — — — S 0.13 0.03 4.5 0.03 0.01 0.004 — 0.1 — — 0.1 0.2 — — — — — — T 0.12 0.02 4.7 0.04 0.01 0.004 — — 0.001 — — — 0.020 — — — — — U 0.13 0.03 4.6 0.03 0.01 0.004 — — — — — — 0.050 — — — — — V 0.12 0.03 4.6 0.03 0.01 0.004 — — — — — — — 0.05 — — — — W 0.13 0.03 4.5 0.02 0.01 0.004 — — — — — — — — 0.05 — — — X 0.12 0.02 4.4 0.03 0.01 0.004 — — — — — — — — — 0.01 — — Y 0.12 0.03 4.5 0.02 0.01 0.004 — — — — — — — — — — 0.01 — Z 0.13 0.02 4.7 0.03 0.01 0.004 — — — — — — — — — — — 0.01 XA 0.02 0.02 4.6 0.03 0.01 0.004 — — — — — — — — — — — — XB 0.36 0.03 4.7 002 0.01 0.004 — — — — — — — — — — — — XC 0.12 0.60 4.5 0.03 0.01 0.004 — — — — — — — — — — — — XD 0.13 0.03 3.5 0.03 0.01 0.004 — — — — — — — — — — — — XE 0.12 0.03 4.6 1.18 0.01 0.004 — — — — — — — — — — — — XF 0.13 0.02 4.5 0.03 0.12 0.004 — — — — — — — — — — — — XG 0.12 0.02 4.7 0.04 0.01 0.020 — — — — — — — — — — — — An underlined portion indicates a value out of the range according to the invention.

Subsequently, the cold-rolled steel sheets and the hot-rolled steel sheets obtained as described above were charged into continuous annealing equipment. In the annealing equipment, as indicated in Tables 2 and 3 (Table 2-1 and Table 2-2 are combined to form Table 2 and Table 3-1 and Table 3-2 are combined to form Table 3), the heating rate in a steel sheet temperature range in the annealing furnace of 450° C. or higher and A° C. or lower (A: 500≦A), the dew point and the traveling time of the steel sheet in a temperature range of 600° C. or higher and 750° C. or lower, and the maximum end-point temperature of the steel sheet were controlled while the steel sheets were passed through the annealing equipment to perform annealing. The dew point in ranges in the annealing furnace other than those in which the dew point was controlled as described above was −35° C. The dew point was controlled by removing water in the atmosphere by absorption. In addition, in the examples, the gas composition of the atmospheric gas contained nitrogen gas, hydrogen gas, and inevitable impurities. The hydrogen concentration in the atmosphere was 10 vol %.

Water quenching following continuous annealing had been performed, tempering was performed at a temperature of 300° C. for 140 seconds. In the examples other than Nos. 32 through 35, the high-strength steel sheets obtained by performing tempering as described above were used as samples. In example Nos. 32 through 35, after tempering as described above had been performed, by subsequently performing electrolytic pickling in an aqueous solution containing 5 mass % of sulfuric acid and having a temperature of 40° C. with current densities given in Table 2, samples were obtained. In electrolytic pickling, alternate current electrolysis was performed with the sample being set at the anode and the cathode in this order for 3 seconds each.

The TS and El of the samples obtained as described above were determined. In addition, phosphatability, corrosion resistance after electrodeposition coating had been performed, and workability were investigated. In addition, the amount of oxides (the amount of internal oxides) existing in the surface of the steel sheet within 100 μm from the surface of the steel sheet was determined. The results are given in Tables 2 and 3. In addition, the methods for the determination and the evaluation criteria will be described hereafter.

Tensile Strength (TS) and Elongation (El)

By using a Metallic materials-Tensile testing-Method prescribed in JIS Z 2241, tensile strength (TS) and elongation (El) were determined. The determined results were used for the evaluation of workability described below.

Phosphatability

The evaluation method of phosphatability was as follows. A chemical conversion treatment was performed by using a chemical conversion treatment solution (PALBOND L-3080 (registered trademark)) produced by Nihon Parkerizing Co., Ltd. as a chemical conversion treatment solution and by using the method described below.

The sample was degreased by using a degreasing solution FINECLEANER (registered trademark) produced by Nihon Parkerizing Co., Ltd., then washed with water, then subjected to surface conditioning for 30 seconds by using a surface conditioning solution PREPALENE-Z (registered trademark) produced by Nihon Parkerizing Co., Ltd. After surface conditioning had been performed, the sample was immersed in the chemical conversion treatment solution (PALBOND L-3080) having a temperature of 43° C. for 120 seconds, then washed with water, and then dried with hot air.

Randomly selected five fields of view of each of the samples which had been subjected to a chemical conversion treatment were observed by using a scanning electron microscope (SEM) at a magnification of 500 times. By determining the area ratio of a lack of hiding of the chemical conversion film by using image analysis, evaluation was performed on the basis of the area ratio of a lack of hiding as described below. “A” corresponds to a satisfactory level.

A: 10% or less

C: more than 10%

Corrosion Resistance after Electrodeposition Coating has been Performed

A test piece of 70 mm×150 mm was taken from the steel sheet which had been subjected to a chemical conversion treatment by using the method described above, and subjected to cation electrodeposition coating (baking condition: 170° C.×20 minutes, film thickness: 25 μm) by using the PN-150G (registered trademark) produced by Nippon Paint Co., Ltd. Subsequently, the end surfaces and the surface which was not to be evaluated were sealed with Al tapes, and the test piece was subjected to cross cut (crossing angle: 60°) reaching the steel sheet surface by using a cutter knife to obtain a test sample.

Subsequently, the test sample was immersed in a 5%-NaCl aqueous solution (55° C.) for 240 hours, then taken out of the solution, then washed with water, then dried, and then subjected to a tape peeling test for the cross-cut portions to determine a peeling width. The determined results were evaluated on the basis of the evaluation criteria described below. “A” corresponds to a satisfactory level.

A: peeling width is less than 2.5 mm per side

C: peeling width is 2.5 mm or more per side

Workability

A tensile test was performed with a constant crosshead speed of 10 mm/min in accordance with the prescription in JIS Z 2241 on a JIS No. 5 tensile test piece which had been taken from the sample in the direction at a right angle to the rolling direction to determine tensile strength TS (MPa) and elongation El (%), and when TS×El was 24000 or more was judged as good in terms of workability while when TS×El was less than 24000 was judged as poor in terms of workability.

Amount of Internal Oxides in a Region within 100 μm of Surface Layer of a Steel Sheet

The amount of internal oxides was determined by using an “impulse furnace melting-infrared absorption method”. It was necessary to subtract the amount of oxygen of the raw material (that is, a steel sheet which had not been subjected to annealing). The amount of oxygen OH contained in the raw material was defined as a determined value obtained by performing polishing to take off the surface layers having a thickness of 100 μm each or more on both surfaces of the high-strength steel sheet which had been subjected to continuous annealing and by determining the oxygen concentration in steel. In addition, the amount of oxygen OI after internal oxidation had been performed was defined as a determined value obtained by determining the oxygen concentration in steel in the whole thickness of the high-strength steel sheet which had been subjected to continuous annealing. The amount of internal oxides was defined as a converted value obtained by using the amount of oxygen OI of the high-strength steel sheet after internal oxidation had been performed and the amount of oxygen OH contained in the raw material, by calculating the difference between OI and OH (=OI−OH), and by converting the difference into a value per unit area (that is, 1 m²) per side (g/m²).

Evaluation of Existence of Internal Oxides in a Region within 10 μm from the Surface and Evaluation of Existence of Mn Oxides in an Intra-Grain Region within 1 μm from the Grain Boundary

By observing randomly selected five fields of view by performing SEM observation or TEM observation at a magnification of 20000 times, and by performing EDX analysis as needed, the evaluation was performed.

The results obtained as described above are given in Tables 2 and 3 along with the manufacturing conditions.

TABLE 2 Annealing Furnace Heating Rate Maximum Steel Sheet Steel from 450° C. to Dew Point End-Point Traveling Time Si Mn A° C. from 600° C. to Temperature through 600° C. to No. Code (mass %) (mass %) (° C./sec.) A (° C.) 750° C. (° C.) (° C.) 750° C. (min.) Note 1 A 0.03 4.5  1 575 −6 630 1.5 Comparative Example 2 A 0.03 4.5  3 575 −6 630 1.5 Comparative Example 3 A 0.03 4.5  5 575 −6 630 1.5 Comparative Example 4 A 0.03 4.5  7 575 −6 630 1.5 Example 5 A 0.03 4.5 10 575 −6 630 1.5 Example 6 A 0.03 4.5 10 575 −6 630 1.5 Example 7 A 0.03 4.5 30 575 −6 630 1.5 Example 8 A 0.03 4.5 100  575 −6 630 1.5 Example 9 A 0.03 4.5 10 575 −35  630 1.5 Comparative Example 10 A 0.03 4.5 10 575 −25  630 1.5 Comparative Example 11 A 0.03 4.5 10 575 −15  630 1.5 Comparative Example 12 A 0.03 4.5 10 575 −11  630 1.5 Comparative Example 13 A 0.03 4.5 10 450 −6 630 1.5 Comparative Example 14 A 0.03 4.5 10 490 −6 630 1.5 Comparative Example 15 A 0.03 4.5 10 500 −6 630 1.5 Example 16 A 0.03 4.5 10 550 −6 630 1.5 Example 17 A 0.03 4.5 10 600 −6 630 1.5 Example 18 A 0.03 4.5 10 575 −6 550 1.5 Comparative Example 19 A 0.03 4.5 10 575 −6 590 1.5 Comparative Example 20 A 0.03 4.5 10 575 −6 600 1.5 Example 21 A 0.03 4.5 10 575 −6 650 1.5 Example 22 A 0.03 4.5 10 575 −6 700 1.5 Example 23 A 0.03 4.5 10 575 −6 750 1.5 Example 24 A 0.03 4.5 10 575 −6 760 1.5 Comparative Example 25 A 0.03 4.5 10 575 −6 800 1.5 Comparative Example 26 A 0.03 4.5 10 575 −6 630 0.1 Comparative Example 27 A 0.03 4.5 10 575 −6 630 0.4 Comparative Example 28 A 0.03 4.5 10 575 −6 630 0.5 Example 29 A 0.03 4.5 10 575 −6 630 1.0 Example 30 A 0.03 4.5 10 575 −6 630 5.0 Example 31 A 0.03 4.5 10 575 −6 630 10.0  Example 32 A 0.03 4.5 10 575 −6 630 15.0  Example 33 A 0.03 4.5 10 575 −6 630 1.5 Example 34 A 0.03 4.5 10 575 −6 630 1.5 Example 35 A 0.03 4.5 10 575 −6 630 1.5 Example 36 A 0.03 4.5 10 575 −6 630 1.5 Example 37 B 0.03 4.6 10 575 −6 630 1.5 Example 38 C 0.03 4.7 10 575 −6 630 1.5 Example 39 D 0.1 4.5 10 575 −6 630 1.5 Example 40 E 0.3 4.7 10 575 −6 630 1.5 Example 41 F 0.5 4.6 10 575 −6 630 1.5 Example 42 G 0.03 3.6 10 575 −6 630 1.5 Example 43 H 0.03 6.3 10 575 −6 630 1.5 Example 44 I 0.03 8.0 10 575 −6 630 1.5 Example 45 J 0.03 4.5 10 575 −6 630 1.5 Example 46 K 0.03 4.6 10 575 −6 630 1.5 Example Internal Oxide within 10 μm of Surface Amount of Existence of Internal Mn Oxide in Tempering Oxide within Intra-grain 300° C. × Electrolytic Corrosion 100 μm Region within 140 sec. Pickling Current Resistance after of Surface Done or 1 μm from Done or (Done or Density Electrodeposition TS El No. (g/m²) Undone Grain Boundary Undone Undone) (A/dm²) Phosphatability Coating (MPa) (%) TS × EL Workability Note 1 0.033 A A Done Undone — C C 1030 25.5 26265 Good Comparative Example 2 0.038 A A Done Undone — C C 1036 25.0 25900 Good Comparative Example 3 0.034 A A Done Undone — C C 1039 24.6 25559 Good Comparative Example 4 0.036 A A Done Undone — A A 1040 25.0 26000 Good Example 5 0.034 A A Done Undone — A A 1038 25.1 26054 Good Example 6 0.033 A A Undone Undone — A A 1035 25.2 26082 Good Example 7 0.035 A A Done Undone — A A 1003 24.8 24874 Good Example 8 0.037 A A Done Undone — A A 1021 24.5 25015 Good Example 9 0.003 C C Done Undone — C C 1020 24.6 25092 Good Comparative Example 10 0.004 C C Done Undone — C C 1024 23.9 24474 Good Comparative Example 11 0.006 C C Done Undone — C C 1035 24.9 25772 Good Comparative Example 12 0.009 C C Done Undone — C C 1040 26.5 27560 Good Comparative Example 13 0.037 A A Done Undone — C C 1046 26.3 27510 Good Comparative Example 14 0.035 A A Done Undone — C C 1005 25.1 25226 Good Comparative Example 15 0.039 A A Done Undone — A A 1023 24.9 25473 Good Example 16 0.040 A A Done Undone — A A 1038 25.8 26780 Good Example 17 0.037 A A Done Undone — A A 1044 25.0 26100 Good Example 18 0.035 A A Done Undone — A A 1006 22.0 22132 Poor Comparative Example 19 0.036 A A Done Undone — A A 1030 23.2 23896 Poor Comparative Example 20 0.033 A A Done Undone — A A 1031 24.6 25363 Good Example 21 0.037 A A Done Undone — A A 1021 24.5 25015 Good Example 22 0.038 A A Done Undone — A A 1055 25.6 27008 Good Example 23 0.033 A A Done Undone — A A 1052 25.8 27142 Good Example 24 0.036 A A Done Undone — C C 712 40.1 28551 Good Comparative Example 25 0.034 A A Done Undone — C C 1331 19.2 25555 Good Comparative Example 26 0.038 A A Done Undone — A A 1007 22.5 22658 Poor Comparative Example 27 0.034 A A Done Undone — A A 1029 23.3 23976 Poor Comparative Example 28 0.036 A A Done Undone — A A 1038 25.5 26469 Good Example 29 0.035 A A Done Undone — A A 1034 24.8 25643 Good Example 30 0.034 A A Done Undone — A A 1029 25.6 26342 Good Example 31 0.038 A A Done Undone — A A 1031 25.8 26600 Good Example 32 0.034 A A Done Undone — A A 1033 25.5 26342 Good Example 33 0.039 A A Done Done 1 A A 1044 25.6 26726 Good Example 34 0.032 A A Done Done 3 A A 1030 25.1 25853 Good Example 35 0.038 A A Done Done 5 A A 1039 25.2 26183 Good Example 36 0.037 A A Done Done 10  A A 1036 25.9 26832 Good Example 37 0.039 A A Done Undone — A A 681 40.3 27444 Good Example 38 0.036 A A Done Undone — A A 1322 19.0 25118 Good Example 39 0.034 A A Done Undone — A A 1053 24.1 25377 Good Example 40 0.035 A A Done Undone — A A 754 36.2 27295 Good Example 41 0.033 A A Done Undone — A A 1049 25.1 26330 Good Example 42 0.034 A A Done Undone — A A 1053 24.6 25904 Good Example 43 0.034 A A Done Undone — A A 1052 24.5 25774 Good Example 44 0.036 A A Done Undone — A A 1056 24.1 25450 Good Example 45 0.035 A A Done Undone — A A 1059 24.9 26369 Good Example 46 0.037 A A Done Undone — A A 1049 24.6 25805 Good Example An underlined portion indicates a value out of the range according to the invention.

TABLE 3 Annealing Furnace Heating Rate Maximum Steel Sheet Steel from 450° C. to Dew Point End-Point Traveling Time Si Mn A° C. from 600° C. to Temperature through 600° C. to No. Code (mass %) (mass %) (° C./sec.) A (° C.) 750° C. (° C.) (° C.) 750° C. (min.) Note 47 L 0.03 4.7 10 575 −6 630 1.5 Example 48 M 0.03 4.5 10 575 −6 630 1.5 Example 49 N 0.02 4.7 10 575 −6 630 1.5 Example 50 O 0.03 4.6 10 575 −6 630 1.5 Example 51 P 0.03 4.5 10 575 −6 630 1.5 Example 52 Q 0.02 4.7 10 575 −6 630 1.5 Example 53 R 0.03 4.5 10 575 −6 630 1.5 Example 54 S 0.03 4.5 10 575 −6 630 1.5 Example 55 T 0.02 4.7 10 575 −6 630 1.5 Example 56 U 0.03 4.6 10 575 −6 630 1.5 Example 57 XA 0.02 4.6 10 575 −6 630 1.5 Comparative Example 58 XB 0.03 4.7 10 575 −6 630 1.5 Comparative Example 59 XC 0.6  4.5 10 575 −6 630 1.5 Comparative Example 60 XD 0.03 3.5 10 575 −6 630 1.5 Comparative Example 61 XE 0.03 4.6 10 575 −6 630 1.5 Comparative Example 62 XF 0.02 4.5 10 575 −6 630 1.5 Comparative Example 63 XG 0.02 4.7 10 575 −6 630 1.5 Comparative Example 64 E 0.3  4.7 10 575 −6 630 1.5 Example 65 F 0.5  4.6 10 575 −6 630 1.5 Example 66 G 0.03 3.6 10 575 −6 630 1.5 Example 67 H 0.03 6.3 10 575 −6 630 1.5 Example 68 I 0.03 8.0 10 575 −6 630 1.5 Example 69 J 0.03 4.5 10 575 −6 630 1.5 Example 70 K 0.03 4.6 10 575 −6 630 1.5 Example 71 L 0.03 4.7 10 575 −6 630 1.5 Example 72 M 0.03 4.5 10 575 −6 630 1.5 Example 73 N 0.02 4.7 10 575 −6 630 1.5 Example 74 O 0.03 4.6 10 575 −6 630 1.5 Example 75 P 0.03 4.5 10 575 −6 630 1.5 Example 76 Q 0.02 4.7 10 575 −6 630 1.5 Example 77 R 0.03 4.5 10 575 −6 630 1.5 Example 78 S 0.03 4.5 10 575 −6 630 1.5 Example 79 T 0.02 4.7 10 575 −6 630 1.5 Example 80 U 0.03 4.6 10 575 −6 630 1.5 Example 81 V 0.03 4.6 10 575 −6 630 1.5 Example 82 W 0.03 4.5 10 575 −6 630 1.5 Example 83 X 0.02 4.4 10 575 −6 630 1.5 Example 84 Y 0.03 4.5 10 575 −6 630 1.5 Example 85 Z 0.02 4.7 10 575 −6 630 1.5 Example 86 XA 0.02 4.6 10 575 −6 630 1.5 Comparative Example 87 XB 0.03 4.7 10 575 −6 630 1.5 Comparative Example 88 XC 0.6  4.5 10 575 −6 630 1.5 Comparative Example 89 XD 0.03 3.5 10 575 −6 630 1.5 Comparative Example 90 XE 0.03 4.6 10 575 −6 630 1.5 Comparative Example 91 XF 0.02 4.5 10 575 −6 630 1.5 Comparative Example 92 XG 0.02 4.7 10 575 −6 630 1.5 Comparative Example Internal Oxide within 10 μm of Surface Amount of Existence of Internal Mn Oxide in Tempering Oxide within Intra-grain 300° C. × Electrolytic Corrosion 100 μm Region within 140 sec. Pickling Current Resistance after of Surface Done or 1 μm from Done or (Done or Density Electrodeposition TS El No. (g/m²) Undone Grain Boundary Undone Undone) (A/dm²) Phosphatability Coating (MPa) (%) TS × EL Workability Note 47 0.038 A A Done Undone — A A 1044 24.0 25056 Good Example 48 0.039 A A Done Undone — A A 1046 24.7 25836 Good Example 49 0.035 A A Done Undone — A A 1050 24.1 25305 Good Example 50 0.035 A A Done Undone — A A 1058 24.5 25921 Good Example 51 0.035 A A Done Undone — A A 1047 24.9 26070 Good Example 52 0.039 A A Done Undone — A A 1045 23.8 24871 Good Example 53 0.036 A A Done Undone — A A 1029 24.0 24696 Good Example 54 0.039 A A Done Undone — A A 1039 24.9 25871 Good Example 55 0.038 A A Done Undone — A A 1046 24.6 25732 Good Example 56 0.039 A A Done Undone — A A 1045 26.0 27170 Good Example 57 0.036 A A Done Undone — A A 602 37.5 22575 Poor Comparative Example 58 0.038 A A Done Undone — A A 1422 16.4 23321 Poor Comparative Example 59 0.039 A A Done Undone — C C 1065 24.6 26199 Good Comparative Example 60 0.031 A A Done Undone — A A 1077 21.0 22617 Poor Comparative Example 61 0.036 A A Done Undone — C C 1071 24.6 26347 Good Comparative Example 62 0.041 A A Done Undone — C C 1046 22.5 23535 Poor Comparative Example 63 0.040 A A Done Undone — A C 1048 19.9 20855 Poor Comparative Example 64 0.039 A A Done Undone — A A 780 36.1 28158 Good Example 65 0.035 A A Done Undone — A A 1049 25.1 26330 Good Example 66 0.036 A A Done Undone — A A 1052 24.6 25879 Good Example 67 0.037 A A Done Undone — A A 1056 24.5 25872 Good Example 68 0.038 A A Done Undone — A A 1054 24.1 25401 Good Example 69 0.040 A A Done Undone — A A 1049 24.7 25910 Good Example 70 0.038 A A Done Undone — A A 1044 23.9 24952 Good Example 71 0.039 A A Done Undone — A A 1043 23.8 24823 Good Example 72 0.040 A A Done Undone — A A 1050 23.4 24570 Good Example 73 0.036 A A Done Undone — A A 1049 23.5 24652 Good Example 74 0.037 A A Done Undone — A A 1047 24.0 25128 Good Example 75 0.035 A A Done Undone — A A 1044 24.6 25682 Good Example 76 0.039 A A Done Undone — A A 1040 23.8 24752 Good Example 77 0.036 A A Done Undone — A A 1039 24.1 25040 Good Example 78 0.039 A A Done Undone — A A 1038 25.0 25950 Good Example 79 0.041 A A Done Undone — A A 1046 24.6 25732 Good Example 80 0.039 A A Done Undone — A A 1041 24.7 25713 Good Example 81 0.040 A A Done Undone — A A 1043 26.3 27431 Good Example 82 0.038 A A Done Undone — A A 1042 26.1 27196 Good Example 83 0.039 A A Done Undone — A A 1040 25.8 26832 Good Example 84 0.041 A A Done Undone — A A 1039 26.1 27118 Good Example 85 0.039 A A Done Undone — A A 1032 26.9 27761 Good Example 86 0.036 A A Done Undone — A A 602 37.1 22334 Poor Comparative Example 87 0.037 A A Done Undone — A A 1420 15.6 22152 Poor Comparative Example 88 0.039 A A Done Undone — C C 1069 24.1 25763 Good Comparative Example 89 0.032 A A Done Undone — A A 1062 19.8 21028 Poor Comparative Example 90 0.034 A A Done Undone — C C 1058 23.4 24757 Good Comparative Example 91 0.039 A A Done Undone — C C 1040 21.9 22776 Poor Comparative Example 92 0.037 A A Done Undone — A C 1037 19.8 20533 Poor Comparative Example An underlined portion indicates a value out of the range according to the invention.

As Tables 2 and 3 indicate, it is clarified that the high-strength steel sheets manufactured by using our method were excellent in terms of phosphatability, corrosion resistance, and workability despite containing a large amount of easily oxidizable chemical elements such as Si and Mn. On the other hand, the comparative examples were poor in terms of one or more of phosphatability, corrosion resistance, and workability.

INDUSTRIAL APPLICABILITY

Since our high-strength steel sheet is excellent in terms of phosphatability, corrosion resistance, and workability, it is possible to use the steel sheet as a surface-treated steel sheet for the weight reduction and strengthening of automobile bodies. Also, it is possible to use the steel sheet as a surface-treated steel sheet, which is manufactured by providing a raw material steel sheet with rust prevention capability, in wide fields such as domestic electrical appliance and architectural material industries in addition to automobile industry. 

1.-4. (canceled)
 5. A method of manufacturing a high-strength steel sheet, comprising: when a steel sheet having a chemical composition containing, by mass %, C: 0.03% or more and 0.35% or less, Si: 0.01% or more and 0.50% or less, Mn: 3.6% or more and 8.0% or less, Al: 0.01% or more and 1.0% or less, P: 0.10% or less, S: 0.010% or less, and the balance being Fe and inevitable impurities is annealed in a continuous annealing process, heating the steel sheet in a heating process of the continuous annealing process at a heating rate of 7° C./sec. or more in a temperature range in an annealing furnace of 450° C. or higher and A° C. or lower (A: 500≦A), controlling a maximum end-point temperature of a steel sheet in the continuous annealing process to 600° C. or higher and 750° C. or lower, and controlling, in a steel sheet temperature range of 600° C. or higher and 750° C. or lower in the continuous annealing process, a traveling time of the steel sheet through the temperature range to 30 seconds or more and 10 minutes or less and a dew point of an atmosphere to −10° C. or higher in the temperature range.
 6. The method according to claim 5, the steel sheet having the chemical composition further containing, by mass %, one or more chemical elements selected from among B: 0.001% or more and 0.005% or less, Nb: 0.005% or more and 0.05% or less, Ti: 0.005% or more and 0.05% or less, Cr: 0.001% or more and 1.0% or less, Mo: 0.05% or more and 1.0% or less, Cu: 0.05% or more and 1.0% or less, Ni: 0.05% or more and 1.0% or less, Sn: 0.001% or more and 0.20% or less, Sb: 0.001% or more and 0.20% or less, Ta: 0.001% or more and 0.10% or less, W: 0.001% or more and 0.10% or less, and V: 0.001% or more and 0.10% or less.
 7. The method according to claim 5, further comprising performing electrolytic pickling in an aqueous solution containing sulfuric acid after the continuous annealing process has been performed.
 8. A high-strength steel sheet having the chemical composition according to claim 5, the oxides of at least one or more selected from among Fe, Si, Mn, Al, P, B, Nb, Ti, Cr, Mo, Cu, Ni, Sn, Sb, Ta, W, and V in an amount of 0.010 g/m² or more and 0.050 g/m² or less per side in total in a region within 100 μm from a surface of the steel sheet, and oxides containing Mn in an intra-grain region within 1 μm from a grain boundary of a steel sheet crystal grain existing in a region within 10 μm from the surface of the steel sheet.
 9. The method according to claim 6, further comprising performing electrolytic pickling in an aqueous solution containing sulfuric acid after the continuous annealing process has been performed.
 10. A high-strength steel sheet having the chemical composition according to claim 6, the oxides of at least one or more selected from among Fe, Si, Mn, Al, P, B, Nb, Ti, Cr, Mo, Cu, Ni, Sn, Sb, Ta, W, and V in an amount of 0.010 g/m² or more and 0.050 g/m² or less per side in total in a region within 100 μm from a surface of the steel sheet, and oxides containing Mn in an intra-grain region within 1 μm from a grain boundary of a steel sheet crystal grain existing in a region within 10 μm from the surface of the steel sheet. 